CN102925812A - Hot rolling diaphragm spring steel for automobile and production method of hot rolling diaphragm spring - Google Patents
Hot rolling diaphragm spring steel for automobile and production method of hot rolling diaphragm spring Download PDFInfo
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- 229910000639 Spring steel Inorganic materials 0.000 title claims abstract description 18
- 238000005098 hot rolling Methods 0.000 title claims abstract description 15
- 238000004519 manufacturing process Methods 0.000 title abstract description 19
- 229910000831 Steel Inorganic materials 0.000 claims abstract description 79
- 239000010959 steel Substances 0.000 claims abstract description 79
- 238000005496 tempering Methods 0.000 claims abstract description 26
- 238000001816 cooling Methods 0.000 claims abstract description 21
- 238000000137 annealing Methods 0.000 claims abstract description 20
- 238000010791 quenching Methods 0.000 claims abstract description 17
- 238000005096 rolling process Methods 0.000 claims abstract description 16
- 238000000034 method Methods 0.000 claims abstract description 15
- 238000010438 heat treatment Methods 0.000 claims abstract description 14
- 238000012545 processing Methods 0.000 claims abstract description 14
- 230000000171 quenching effect Effects 0.000 claims abstract description 14
- 238000005266 casting Methods 0.000 claims abstract description 5
- 229910052804 chromium Inorganic materials 0.000 claims abstract description 5
- 229910052750 molybdenum Inorganic materials 0.000 claims abstract description 5
- 229910052720 vanadium Inorganic materials 0.000 claims abstract description 5
- 238000003723 Smelting Methods 0.000 claims abstract description 4
- 238000009413 insulation Methods 0.000 claims abstract description 4
- 238000007670 refining Methods 0.000 claims abstract description 4
- 229910052757 nitrogen Inorganic materials 0.000 claims abstract description 3
- XEEYBQQBJWHFJM-UHFFFAOYSA-N iron Substances [Fe] XEEYBQQBJWHFJM-UHFFFAOYSA-N 0.000 claims description 10
- 229910052748 manganese Inorganic materials 0.000 claims description 6
- 229910052698 phosphorus Inorganic materials 0.000 claims description 6
- 229910052717 sulfur Inorganic materials 0.000 claims description 6
- 238000009749 continuous casting Methods 0.000 claims description 5
- 230000006698 induction Effects 0.000 claims description 4
- 229910052710 silicon Inorganic materials 0.000 claims description 4
- 238000010583 slow cooling Methods 0.000 claims description 4
- 238000003756 stirring Methods 0.000 claims description 4
- 230000003009 desulfurizing effect Effects 0.000 claims description 3
- 229910052742 iron Inorganic materials 0.000 claims description 3
- 238000012856 packing Methods 0.000 claims description 3
- 230000011218 segmentation Effects 0.000 claims description 3
- 238000007493 shaping process Methods 0.000 claims description 3
- XLYOFNOQVPJJNP-UHFFFAOYSA-N water Substances O XLYOFNOQVPJJNP-UHFFFAOYSA-N 0.000 claims description 3
- 238000010008 shearing Methods 0.000 abstract description 3
- FBPFZTCFMRRESA-JGWLITMVSA-N D-glucitol Chemical group OC[C@H](O)[C@@H](O)[C@H](O)[C@H](O)CO FBPFZTCFMRRESA-JGWLITMVSA-N 0.000 abstract description 2
- 238000001556 precipitation Methods 0.000 abstract description 2
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- 229910052799 carbon Inorganic materials 0.000 description 8
- OKTJSMMVPCPJKN-UHFFFAOYSA-N Carbon Chemical compound [C] OKTJSMMVPCPJKN-UHFFFAOYSA-N 0.000 description 7
- 238000007669 thermal treatment Methods 0.000 description 6
- 230000002929 anti-fatigue Effects 0.000 description 4
- 239000000203 mixture Substances 0.000 description 4
- 238000005204 segregation Methods 0.000 description 4
- 239000000126 substance Substances 0.000 description 4
- 229910001566 austenite Inorganic materials 0.000 description 3
- 229910001567 cementite Inorganic materials 0.000 description 3
- 230000000052 comparative effect Effects 0.000 description 3
- 238000013461 design Methods 0.000 description 3
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- 239000002131 composite material Substances 0.000 description 1
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Abstract
The invention discloses hot rolling diaphragm spring steel for an automobile and a production method of the hot rolling diaphragm spring steel. The hot rolling diaphragm spring steel comprises the following components by weight percentage: 0.40-0.60% of C, 0.15-0.35% of Si, 0.70-1.20% of Mn, less than or equal to 0.015% of P, less than or equal to 0.008% of S, less than or equal to 0.050% of Alt, 0.10-0.30% of Mo, 0.70-1.20% of Cr, 0.10-0.50% of V and less than or equal to 0.005% N. The production method comprises the processing steps of desulfurating, smelting, refining, conducting vacuum treatment, continuously casting to form a blank, conducting segmented thermal insulation according to temperature, heating the casting blank, rolling, coiling, slowly cooling, shearing a steel band, annealing, molding, quenching, tempering and waiting for application. According to the hot rolling diaphragm spring steel and the production method, the production cost is low; a load of a rolling mill can be reduced; the comprehensive mechanical property is excellent; a steel coil is heated uniformly in the annealing process; the uniformity of a metallurgical structure is ensured; a tempered sorbite structure is obtained by heat treatment of the quenching and the tempering; the steel is separated out by compound precipitation of microalloys, such as Cr, Mo and V in the steel; and high strength and good wear-proof property of the steel are ensured.
Description
Technical field
The present invention relates to spring steel, be specifically used for automobile hot rolling diaphragm spring steel and production method thereof.
Background technology
Before the present invention proposed, the similar technical products that relates to alloy structure steel making field was more, but less for automobile diaphragm spring steel aspect.Through retrieval, the Chinese patent name is called " high tough high-hardenability spring tube material ", and number of patent application is the document of CN200510018800.7, its composition and mass percent C:0.48 ~ 0.55%, Si:0.17 ~ 0.37%, Mn:0.70 ~ 1.00%, Cr:0.8 ~ 1.1%, B:0.001 ~ 0.004%, Ni≤0.35%, Cu≤0.25%, P≤0.03%, S≤0.03%, all the other are Fe.It has been owing to having added B, and P, S content control level are not high, though have certain economy, the post-production poor-performing can not satisfy automobile diaphragm spring with the requirement of steel.And this steel is when quenching, and intensity can obtain larger raising, and crack sensitivity is also higher, easily at the subsequent disposal Fracture, has increased heat treated difficulty.
Japanese documentation JP19930037451 " a kind of clutch diaphragm steel " and JP19890059067 " a kind of Automobile Clutch Plate Spring steel ", these two kinds of steel on chemical composition owing to all having added more C, Si, Mn and a certain amount of Mo, cause that not only production cost is high, and production unit is had relatively high expectations, and the post-production difficulty is also larger.
In the automobile clutch assembly, diaphragm spring has a significant impact the performance and used life in the automobile clutch assembly.At present, limit by metallurgical equipment ability level and post-production level, domestic large-scale cargo truck and high-grade car diaphragm spring major part also adopt imported materials and items.Domestic automobile diaphragm spring steel adopts the operational path of " hot rolling → annealing → shearing → thermal treatment " more, process again and thermal treatment after the intensity by anneal reduction steel, but the product performance homogeneity is bad, but its product comprehensive mechanical property and do not reach high-grade automobile clutch work-ing life with the requirement of steel.In order further to improve automobile diaphragm spring elastic force, cold and hot working performance, work-ing life, reduce the plate property fluctuation, realize the production domesticization of this steel grade, finish the history of large-scale cargo truck diaphragm spring dependence on import, project verification research and development automobile diaphragm spring steel.Improve automobile diaphragm spring elastic force, cold and hot working performance, work-ing life for further, and reduce the plate property fluctuation, propose the present invention for this reason.
Summary of the invention
The purpose of this invention is to provide a kind of automobile hot rolling diaphragm spring steel and manufacture method thereof, can overcome the rear coil of strip tissue of annealing and mechanical property lack of homogeneity, surface quality is bad and cold-forming property not enough, obtains automobile hot rolling diaphragm spring steel and the production method thereof of high strength, high elastic limit, high yield strength and highly anti-fatigue limiting performance.
Realize the measure of above-mentioned purpose:
A kind of automobile hot rolling diaphragm spring steel, its component and weight percent content are: C:0.40 ~ 0.60%, Si:0.15 ~ 0.35%, Mn:0.70 ~ 1.20%, P≤0.015%, S≤0.008%, Alt≤0.050%, Mo:0.10 ~ 0.30%, Cr:0.70 ~ 1.20%, V:0.10 ~ 0.50%, N≤0.005%, surplus is Fe and inevitably is mingled with.
Produce a kind of automobile method of hot rolling diaphragm spring steel, its step:
1) carries out desulfurizing iron;
2) carry out converter smelting;
3) in the LF stove, carry out refining;
4) process in the RH vacuum oven, the control vacuum processing time is no less than 18 minutes;
5) continuous casting becomes base: induction stirring all the time in casting process;
6) in stay-warm case strand is carried out temperature section insulation: when holding temperature during greater than 600 ℃, speed of cooling is not higher than 50 ℃/hour; When holding temperature in 200～600 ℃ of scopes, the speed of cooling scope is at 150 ~ 250 ℃/hour; When holding temperature is lower than 200 ℃, opens stay-warm case and carry out air cooling;
7) to the strand heating, heating and temperature control is 1200～1300 ℃, and heating rate is controlled to be 8～14 minutes/centimetre;
8) carry out segmentation rolling: control roughing start rolling temperature is at 1050～1150 ℃, and control finish rolling finishing temperature is at 850～920 ℃;
9) batch, the control coiling temperature is at 680～780 ℃;
10) carry out slow cooling, speed of cooling is controlled to be no more than to be cooled under 40 ℃/hour and is no more than 200 ℃;
11) shear steel band;
12) anneal, annealing temperature is 700～780 ℃, annealing time: (6+0.5Q) * 60 minute/ton steel,
In the formula, Q represents that the steel plate gross weight of packing into, unit are ton;
13) machine-shaping;
14) quench according to the profiled member different sites: the control quenching temperature is at 820～880 ℃, and the profiled member inner ring adopts oil or quenching medium to carry out, and it is 120～150 ℃/second that speed of cooling is controlled at; The profiled member outer ring adopts water to carry out, and speed of cooling is controlled at 200～300 ℃/second;
15) carry out the tempering of two stages: the fs, tempering temperature is in the time of 450～600 ℃, and tempering time adds 30 minutes for the thickness of slab take millimeter as unit; Subordinate phase, tempering temperature are in the time of 250～400 ℃, and tempering time adds 50 minutes for the thickness of slab take millimeter as unit;
16) check and stand-by.
The function and mechanism of each element and main technologic parameters among the present invention:
The element aspect:
C: it is to improve the most effective element of steel strength, along with the increase of C content, and Fe in the steel
3C increases, and hardenability also increases, and the tensile strength of steel and yield strength improve.But along with C content increases, the unit elongation of steel, impelling strength and cold-forming property descend.Therefore, in conjunction with existing steel grade of the same type, the C content of steel of the present invention should be controlled in 0.45% ~ 0.60%, guarantees that steel plate has high strength, high hardenability, high-wearing feature etc.
Si: the avidity of itself and carbon is very weak, and carburet not in steel, but can dissolve in ferrite produces solution strengthening effect, so that ferritic intensity and hardness improves, but plasticity and toughness descend to some extent.As seen, Si has certain help to intensity, but content can not be too high, in order to avoid reduce the plasticity and toughness of steel.The Si content of steel of the present invention is controlled in 0.15% ~ 0.35% scope and can meets the demands.
Mn: the avidity of itself and carbon is stronger, it is the effective element that enlarges austenite phase region, crystal grain thinning, spheroidized carbide and assurance over-all properties and improve hardening capacity, and it does not worsen the deformability of steel, and 1.00% Mn approximately can be tensile strength contribution 100MPa.Consider the strength range of steel of the present invention, therefore Mn is controlled at 0.70% ~ 1.20%.
Al: it is the main deoxidant element in the steel, and the maxima solubility in austenite is about 0.6%, and it only faintly increases hardening capacity after dissolving in austenite.But when the Al too high levels, easily cause being mingled with in the steel and increase, unfavorable to the toughness of steel, therefore Alt content in the steel is controlled in 0.050%.
Mo: in the higher steel of carbon content, Mo mainly is in order to improve the hardening capacity of steel, improves the secondary hardening ability of steel, and can improve the obdurability of steel, suppresses temper brittleness.Simultaneously, can also improve cementite stability and hardness in the steel, elasticity, wear resistance and the ultimate strength that improves steel played an important role, but content can increase decarburizing tendency when more.Therefore, Mo content is controlled at 0.10% ~ 0.30%.
Cr: the effect that it can improve the hardening capacity of steel and secondary hardening is arranged is the particularly element of hot strength of Effective Raise steel strength, can also improve cementite stability and hardness in the steel, and elasticity, wear resistance and the ultimate strength that improves steel played an important role.Can improve steel anti-hydrogen embrittlement ability and temper resistance.Simultaneously, Cr can also improve the coil of strip surface quality, is convenient to cold rolling processing of later stage.Consider above-mentioned analytical results, and the contents level of Mo in the steel, Cr content is controlled at 0.70% ~ 1.20%.
V: it is one of carbide forming element of Effective Raise armor plate strength, and the effect in steel is only second to Nb, Ti.To form VC after adding V in the steel, improve fusing point, hardness and the wear resistance of cementite.But the content of V can not be too high, and V disperse state occurs when average tempering distributes, and produces secondary hardening, is unfavorable for the inspection during manufacture of steel.Therefore, V is controlled at 0.10% ~ 0.50% during the content of design V.
Although impurity element P, S in steel content in steel is very few, and is larger to the cold and hot working performance impact, strictly controls its content and can obviously reduce phenomenon of rupture in the course of processing.The segregation of P goes out often at brittle failure position that coils of hot-rolled steel occurs, and the segregation that contains the inclusion of S also easily causes that layering is torn etc., and the processing characteristics of steel is had considerable influence.Therefore, P should be controlled in 0.015% for this steel, S is controlled in 0.008%.
In addition, this steel is had relatively high expectations at continuous casting and annealing process, should reduce gas content in the steel as far as possible, reduces the segregation of steel.Simultaneously, in order to reduce the influence of time effect of steel, the content of N is controlled in 0.005%.
Process aspect:
Process for making
The present invention limits the vacuum processing time in the process for making and is no less than 18min, its objective is by increasing vacuum processing time to reduce preferably impurity in the steel, gas content.
Why the present invention will be controlled to be vacuum processing time is not less than 18min, can reduce preferably impurity in the steel, gas content.
Must carry out induction stirring when being defined in continuous casting in addition, be because Carbon Content Of Steel, alloying element content are higher, to reduce element segregation.
Also require strand is taked different slow cooling speed according to the temperature section difference, purpose is avoided the high-temperature embrittlement zone exactly, prevents disconnected base, reduces the strand crackle, improves slab quality.
Steel rolling process
Because hardness of steel of the present invention is high, be rolled and batch by high-strength steel technique.Rolling front slab heating temperature is 1200 ~ 1300 ℃, and heating rate is 8 ~ 14min/cm, guarantees the even steel of strand temperature.When roughing and finish rolling, design temperature is higher than conventional low alloy steel, reduces the milling equipment load.Simultaneously, consider the critical point temperature of steel, avoid occurring mixed crystal phenomenon.Therefore, the roughing start rolling temperature of steel is 1050 ~ 1150 ℃, and the finish rolling finishing temperature is 850 ~ 920 ℃, and coiling temperature is 680 ~ 780 ℃.
Processing, thermal treatment process
Machining process route of the present invention: shear → annealing (carbon atmosphere) → processing → quenching → tempering → the check delivery.Why before annealing, shear, it is the substance for less annealing coil, so that thermal treatment is heated evenly, avoid coil of strip top layer and heart section be heated and speed of cooling inhomogeneous and cause the inhomogeneous of annealed structure, affect the processing of back and the performance after the thermal treatment.When annealing, add carbon dust in the annealing furnace, can effectively avoid coil of strip superficial decarbonization phenomenon, Decarburized layer is dropped in the 20 μ m, reduce decarburization position coil of strip performance ununiformity.Annealing temperature is controlled at 700 ~ 780 ℃, is in order significantly to reduce coil of strip intensity, and so that steel organize nodularization, to be easy to shearing.
Quenching temperature is controlled at 820 ~ 880 ℃, and adopts different cooling systems according to different sites, purpose is exactly for according to the requirement of parts different sites use properties, accurately controls tissue and the mechanical property of different sites, so that parts satisfy service requirements fully.
Adopt the tempering of two stages, the fs tempering temperature is controlled at 450 ~ 600, and employing temperature section and the different mode of the different tempering times of temperature section, in order to allow the steel complete austenitizing, obtain stable tempered martensite behind the quenching+tempering, obtain high strength, snappiness, high yield strength and the highly anti-fatigue limit.Subordinate phase, tempering temperature are controlled at 250～400 ℃, are in order to reduce the internal stress of parts, to prevent from use deforming and rupturing, guaranteeing to use safety.
The present invention compared with prior art not only has high strength, snappiness, high yield strength and the highly anti-fatigue limit, can be used for making the various types of vehicles clutch assembly, particularly large-scale cargo truck and high-grade car.And carbon in Composition Design adopts, and add a certain amount of Mn, Cr, Mo, V, simultaneously strict control P, S content so that production cost reduces, utilize reasonably rollingly and batch system, have reduced mill load and infringement; Designed the operational path of hot rolled coil → cutting → annealing → processing → quenching → tempering in the post-production, by reducing the annealing coil substance, being heated evenly property of coil of strip when having improved annealing, guaranteed homogeneity of structure, and obtain the tempered sorbite tissue by quenching+tempering thermal treatment, utilize the composite precipitation of the microalloies such as Cr in the steel, Mo, V to separate out and guaranteed that steel obtain enough intensity and wear resistance.
Description of drawings
Fig. 1 is As rolled metallographic structure figure of the present invention
Fig. 2 is As rolled cross section metallographic structure figure of the present invention.
Embodiment
The below is described in detail the present invention:
Table 1 is the value tabulation of various embodiments of the present invention and Comparative Examples;
Table 2 is the main technologic parameters tabulation of various embodiments of the present invention and Comparative Examples;
Table 3 is various embodiments of the present invention and Comparative Examples mechanical properties test the results list.
Various embodiments of the present invention are according to following steps production:
Its step:
1) carries out desulfurizing iron;
2) carry out converter smelting;
3) in the LF stove, carry out refining;
4) process in the RH vacuum oven, the control vacuum processing time is no less than 18 minutes;
5) continuous casting becomes base: induction stirring all the time in casting process;
6) in stay-warm case strand is carried out temperature section insulation: when holding temperature during greater than 600 ℃, speed of cooling is not higher than 50 ℃/hour; When holding temperature in 200～600 ℃ of scopes, the speed of cooling scope is at 150 ~ 250 ℃/hour; When holding temperature is lower than 200 ℃, opens stay-warm case and carry out air cooling;
7) to the strand heating, heating and temperature control is 1200～1300 ℃, and heating rate is controlled to be 8～14 minutes/centimetre;
8) carry out segmentation rolling: control roughing start rolling temperature is at 1050～1150 ℃, and control finish rolling finishing temperature is at 850～920 ℃;
9) batch, the control coiling temperature is at 680～780 ℃;
10) carry out slow cooling, speed of cooling is controlled to be no more than to be cooled under 40 ℃/hour and is no more than 200 ℃;
11) shear steel band;
12) anneal, annealing temperature is 700～780 ℃, annealing time: (6+0.5Q) * 60 minute/ton steel,
In the formula, Q represents that the steel plate gross weight of packing into, unit are ton;
13) machine-shaping;
14) quench according to the profiled member different sites: the control quenching temperature is at 820～880 ℃, and the profiled member inner ring adopts oil or quenching medium to carry out, and it is 120～150 ℃/second that speed of cooling is controlled at; The profiled member outer ring adopts water to carry out, and speed of cooling is controlled at 200～300 ℃/second;
15) carry out the tempering of two stages: the fs, tempering temperature is in the time of 450～600 ℃, and tempering time adds 30 minutes for the thickness of slab take millimeter as unit; Subordinate phase, tempering temperature are in the time of 250～400 ℃, and tempering time adds 50 minutes for the thickness of slab take millimeter as unit;
16) check and stand-by.
Table 1 various embodiments of the present invention and contrast steel grade chemical composition (wt%)
Table 2 various embodiments of the present invention and the main processes () that contrasts steel grade
Table 2 various embodiments of the present invention and the heat treatment process (two) that contrasts steel grade
Table 3 various embodiments of the present invention and the mechanical properties test the results list that contrasts steel grade
As can be seen from Table 3, steel grade of the present invention has good cold and hot working performance, and has high strength (R
m: 1500 ~ 2000MPa), snappiness, high yield strength and the highly anti-fatigue limit can be used for making the various types of vehicles clutch assembly, particularly large-scale cargo truck and high-grade car.
Above-described embodiment only exemplifies for the best, and is not to be restriction to embodiments of the present invention.
Claims (2)
1. an automobile is with hot rolling diaphragm spring steel, its component and weight percent content are: C:0.40 ~ 0.60%, Si:0.15 ~ 0.35%, Mn:0.70 ~ 1.20%, P≤0.015%, S≤0.008%, Alt≤0.050%, Mo:0.10 ~ 0.30%, Cr:0.70 ~ 1.20%, V:0.10 ~ 0.50%, N≤0.005%, surplus is Fe and inevitably is mingled with.
2. produce a kind of automobile as claimed in claim 1 method of hot rolling diaphragm spring steel, its step:
1) carries out desulfurizing iron;
2) carry out converter smelting;
3) in the LF stove, carry out refining;
4) process in the RH vacuum oven, the control vacuum processing time is no less than 18 minutes;
5) continuous casting becomes base: induction stirring all the time in casting process;
6) in stay-warm case strand is carried out temperature section insulation: when holding temperature during greater than 600 ℃, speed of cooling is not higher than 50 ℃/hour; When holding temperature in 200～600 ℃ of scopes, the speed of cooling scope is at 150 ~ 250 ℃/hour; When holding temperature is lower than 200 ℃, opens stay-warm case and carry out air cooling;
7) to the strand heating, heating and temperature control is 1200～1300 ℃, and heating rate is controlled to be 8～14 minutes/centimetre;
8) carry out segmentation rolling: control roughing start rolling temperature is at 1050～1150 ℃, and control finish rolling finishing temperature is at 850～920 ℃;
9) batch, the control coiling temperature is at 680～780 ℃;
10) carry out slow cooling, speed of cooling is controlled to be no more than to be cooled under 40 ℃/hour and is no more than 200 ℃;
11) shear steel band;
12) anneal, annealing temperature is 700～780 ℃, annealing time: (6+0.5Q) * 60 minute/ton steel,
In the formula, Q represents that the steel plate gross weight of packing into, unit are ton;
13) machine-shaping;
14) quench according to the profiled member different sites: the control quenching temperature is at 820～880 ℃, and the profiled member inner ring adopts oil or quenching medium to carry out, and it is 120～150 ℃/second that speed of cooling is controlled at; The profiled member outer ring adopts water to carry out, and speed of cooling is controlled at 200～300 ℃/second;
15) carry out the tempering of two stages: the fs, tempering temperature is in the time of 450～600 ℃, and tempering time adds 30 minutes for the thickness of slab take millimeter as unit; Subordinate phase, tempering temperature are in the time of 250～400 ℃, and tempering time adds 50 minutes for the thickness of slab take millimeter as unit;
16) check and stand-by.
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| CN201210462046.6A CN102925812B (en) | 2012-11-16 | 2012-11-16 | Hot rolling diaphragm spring steel for automobile and production method of hot rolling diaphragm spring |
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| CN103898412A (en) * | 2014-03-14 | 2014-07-02 | 山西太钢不锈钢股份有限公司 | Hot rolled strip steel for automobile clutch diaphragm spring and manufacturing method thereof |
| CN104313472A (en) * | 2014-10-31 | 2015-01-28 | 武汉钢铁(集团)公司 | High-carbon hot-rolled automobile diaphragm spring steel and production method thereof |
| CN104668907A (en) * | 2015-01-30 | 2015-06-03 | 南通弘峰机电有限公司 | Machining process for large spring pieces |
| CN105039657A (en) * | 2015-06-29 | 2015-11-11 | 江苏金基特钢有限公司 | Method for improving wear-resisting performance of carbon steel |
| CN105316591A (en) * | 2015-03-14 | 2016-02-10 | 洛阳辰祥机械科技有限公司 | Preparation method for high-performance spring |
| CN105886930A (en) * | 2016-04-26 | 2016-08-24 | 宝山钢铁股份有限公司 | High-strength corrosion-resistant spring steel and manufacturing method thereof |
| CN106222572A (en) * | 2016-08-19 | 2016-12-14 | 武汉钢铁股份有限公司 | A kind of thickness is the manufacture method of the cold rolling medium high carbon alloy structural steel of 0.4 0.8mm |
| CN106222553A (en) * | 2016-08-19 | 2016-12-14 | 武汉钢铁股份有限公司 | A kind of thickness is the manufacture method of the cold rolling medium high carbon alloy structural steel of 0.1 0.4mm |
| CN106311789A (en) * | 2015-06-19 | 2017-01-11 | 常熟宝升精冲材料有限公司 | Fine blanking machining method for spring steel |
| CN107177782A (en) * | 2017-06-30 | 2017-09-19 | 武汉钢铁有限公司 | A kind of corrosion-resistant spring steel and preparation method thereof |
| WO2019007240A1 (en) * | 2017-07-05 | 2019-01-10 | 南京钢铁股份有限公司 | Process for manufacturing sk5 spring steel for automobile safety belt coil spring |
| CN109881117A (en) * | 2019-03-20 | 2019-06-14 | 包头钢铁（集团）有限责任公司 | A kind of high-carbon spring hot-rolled coil and its production method |
| CN110295271A (en) * | 2019-06-19 | 2019-10-01 | 东莞市卓蓝自动化设备有限公司 | A kind of flexbile gear heat treatment process |
| CN110699528A (en) * | 2019-11-12 | 2020-01-17 | 山东汽车弹簧厂淄博有限公司 | Novel spring steel plate preparation method |
| CN111304413A (en) * | 2020-03-13 | 2020-06-19 | 大冶特殊钢有限公司 | Spring flat steel and preparation method thereof |
| WO2020248459A1 (en) * | 2019-06-10 | 2020-12-17 | 育材堂（苏州）材料科技有限公司 | Heat treatment method for high-strength steel and product obtained therefrom |
| CN115078040A (en) * | 2022-07-27 | 2022-09-20 | 广东韶钢松山股份有限公司 | Evaluation method of Soxhlet type zonal tissue |
| CN115786799A (en) * | 2022-11-03 | 2023-03-14 | 山东钢铁股份有限公司 | Production method of medium carbon structural steel without mixed crystal and widmannstatten structure |
| CN115874108A (en) * | 2022-12-21 | 2023-03-31 | 湖南华菱涟源钢铁有限公司 | Method for refining dendritic crystal structure in steel |
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| CN111304413A (en) * | 2020-03-13 | 2020-06-19 | 大冶特殊钢有限公司 | Spring flat steel and preparation method thereof |
| CN115078040A (en) * | 2022-07-27 | 2022-09-20 | 广东韶钢松山股份有限公司 | Evaluation method of Soxhlet type zonal tissue |
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